CN108611588B - High-temperature oxidation resistant and sulfur and chlorine corrosion resistant alloy coating and preparation method thereof - Google Patents
High-temperature oxidation resistant and sulfur and chlorine corrosion resistant alloy coating and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
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- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/12—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the method of spraying
- C23C4/134—Plasma spraying
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
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Abstract
The invention relates to an alloy coating with high temperature oxidation resistance and sulfur and chlorine corrosion resistance and a preparation method thereof, wherein the alloy coating comprises the following components in percentage by weight: 25 wt% -35 wt%, Mo: 10 wt% -30 wt%, Cr: 15 wt% -25 wt%, Al: 3wt% -9 wt%, Si: 1 wt% -4 wt%, Y: 0.1 wt% -0.5 wt%, Co: and (4) the balance.
Description
Technical Field
The invention relates to an alloy coating with high temperature oxidation resistance and sulfur and chlorine corrosion resistance and a preparation method thereof, belonging to the technical field of thermal spraying alloy coatings.
Background
The coke oven is a high-efficiency thermotechnical kiln in the energy conversion device, and the heat loss of the coke oven consists of 4 parts: the heat discharged by the red coke belt accounts for about 37 percent of the heat loss of the coke oven and is recycled by the dry quenching technology; the heat brought out by the coke oven flue gas is about 17 percent and is recycled by coal moisture control or heat pipe technology; the heat loss on the surface of the furnace body accounts for about 10 percent and is reduced by the heat preservation of the furnace body; only the raw gas (gas without purification treatment) which brings about heat loss of about 36 percent is carried out, and the rest heat is not completely recovered. The raw gas is the gas generated in the coal coking process and flows out of the coking chamber through the riser along with the coking process. The waste heat recovery of the raw gas has great significance for energy conservation and emission reduction, is one of effective ways for improving the resource utilization rate of the coking plant, and is also a demand for improving the environment and building a green coking plant.
The temperature resistance and corrosion resistance of the wall material in the riser are one of the technical bottlenecks of the raw gas waste heat recovery. The inner wall is directly contacted with high-temperature (650-850 ℃) raw gas, the raw gas contains oxygen, carbon monoxide, carbon dioxide, hydrogen sulfide, nitrogen oxide, hydrogen, methane, water vapor, hydrogen chloride, aromatic hydrocarbon compounds and the like, and common carbon steel is seriously ablated at high temperature under the temperature and environment and cannot meet the requirements of working conditions. If the material of the inner cylinder is increased, the price is increased rapidly only by adopting special alloy steel which resists high temperature corrosion, such as steel with the Haw 120 level or above. The ascending pipe is communicated with the carbonization chamber, once the ascending pipe is cracked due to local thermal stress concentration, the heat exchange medium is leaked, the heat exchange medium can easily enter the carbonization chamber, the coking process is directly influenced, and production accidents can be caused in serious cases. In addition, coking phenomenon (coal tar and graphite are attached and gathered) can occur on the inner wall of the ascending pipe after the coke oven operates for a certain time. The coking increases the motion resistance of the raw gas in the pipeline, and the gas passage can be blocked to suck the raw gas when the coking is serious. The coating is prepared on the surface of the engineering structure material substrate, and various functional surfaces can be endowed to the engineering material substrate. The thermal spraying technology has the advantages of wide application range of spraying materials, suitability for inner hole spraying, controllable coating thickness, wide range (several micrometers to several millimeters), good process stability, reliable coating quality and the like, becomes an effective process method for preparing the coating, and has been widely applied to the aspects of spaceflight, aviation, automobiles, machinery, energy sources, metallurgy, petrifaction, ships and the like. Thermal spraying is an important means for saving precious materials, saving energy, improving the product quality, prolonging the service life of the product, reducing the cost and improving the efficacy. The inner wall coating of the ascending tube must have the characteristics of high-temperature oxidation resistance and corrosion resistance to meet the complex working condition environment requirement. In addition, the coating also has high heat conduction characteristic so as to recover the waste heat of the raw coke oven gas to the maximum extent and recycle waste heat resources.
At present, researchers design and prepare a ceramic (glaze) coating on the surface of the inner wall of the ascending pipe so as to improve the high-temperature resistance and corrosion resistance of the inner wall. However, the difference between the thermal expansion coefficients of the ceramic material and the metal substrate of the riser is large, and stress is easily generated on a contact interface in the temperature rising and lowering process, which is not favorable for the combination of the ceramic material and the metal substrate of the riser. And the alloy coatings such as NiAl, NiCr, CoNiCrAlY and the like are difficult to achieve satisfactory high-temperature oxidation resistance and corrosion resistance.
Disclosure of Invention
Aiming at the problems in the prior art, the invention aims to provide an alloy coating which has good heat conduction, high-temperature oxidation resistance and corrosion resistance, has higher bonding strength with a metal base material, and can effectively prolong the service life of a riser for raw coke oven gas sensible heat recovery engineering.
Another object of the present invention is to provide a method for preparing an alloy coating that is resistant to high temperature oxidation and corrosion.
In a first aspect, the invention provides an alloy coating resistant to high temperature oxidation and sulfur and chlorine corrosion, which is characterized in that the composition of the alloy coating is CoNiMoCrAlSiY, wherein the ratio of Ni: 25 wt% -35 wt%, Mo: 10 wt% -30 wt%, Cr: 15 wt% -25 wt%, Al: 3wt% -9 wt%, Si: 1 wt% -4 wt%, Y: 0.1 wt% -0.5 wt%, Co: and (4) the balance.
According to the invention, Si is introduced into the CoNiCrAlY alloy coating to promote the formation of a glass phase in the coating, thereby increasing the compactness of the coating and preventing the penetration of a corrosive medium. Mo can further improve the high-temperature oxidation resistance and the corrosion resistance of the alloy coating. In addition, Si and Mo also contribute to improving the bonding property and the anti-coking property of the coating. Therefore, the alloy coating of the invention has unique high temperature resistance, oxidation resistance, corrosion resistance and high heat conduction capability, and has high bonding strength with a substrate, for example, more than 40 MPa. The alloy coating is particularly suitable for being sprayed on the inner wall of the riser for raw gas sensible heat recovery engineering, and the service life of the riser is effectively prolonged.
Preferably, the alloy coating contains: ni: 25 wt% -30 wt%, Mo: 10 wt% -25 wt%, Cr: 15 wt% -20 wt%, Al: 5 wt% -8 wt%, Si: 2-4 wt%, Y: 0.3wt% -0.5 wt%, Co: and (4) the balance.
Preferably, the thickness of the alloy coating is 50 to 350 μm.
In a second aspect, the invention provides a method for preparing any one of the alloy coatings, which comprises spraying a CoNiMoCrAlSiY alloy coating on the surface of a base material by adopting a thermal spraying technology.
According to the preparation method, the CoNiMoCrAlSiY alloy coating with good melting effect and high bonding strength with the base material can be obtained.
Preferably, the thermal spray technique is an atmospheric plasma spray technique.
Preferably, the process parameters of the atmospheric plasma spraying technology include: the plasma gas argon flow is 30-60 slpm, the plasma gas hydrogen flow is 4-10 slpm, the spraying current is 300-600A, the voltage is 30-75V, the powder feeding carrier gas argon flow is 3-4 slpm, and the powder feeding speed is 30-60 g/min.
The substrate may be a metal substrate, preferably the riser inner wall of a coke oven.
Drawings
FIG. 1 is a digital photograph and a cross-sectional SEM photograph of a sample of the coating of example 1.
FIG. 2 is a digital photograph and a cross-sectional SEM picture of a coated coupon after thermal shock for example 2.
FIG. 3 is a SEM picture of a cross-section of a coated sample after service in example 3.
Fig. 4 is a digital photograph of the coated sample of comparative example 1.
Fig. 5 is a digital photograph of a coated sample of comparative example 2.
FIG. 6 is a SEM picture of a cross section of a coated sample of comparative example 6.
Detailed Description
The present invention is further described below in conjunction with the following embodiments and the accompanying drawings, it being understood that the drawings and the following embodiments are illustrative of the invention only and are not limiting thereof.
Disclosed herein is an alloy coating having a composition of CoNiMoCrAlSiY.
The alloy coating contains Si, so that the formation of a glass phase in the coating can be promoted, the compactness of the coating is increased, the penetration of a corrosive medium is blocked, and the bonding performance of the coating is improved. In addition, silicon dioxide generated in the working process of Si can greatly limit the external diffusion of metal elements and the internal diffusion of oxygen and carbon atoms, and is one of the most ideal materials for inhibiting the catalytic coking effect. Therefore, Si contributes to the improvement of the anti-coking properties of the coating. In some embodiments, the amount of Si in the alloy coating may be 1 wt% to 4 wt%. If the Si content is less than 1 wt%, it is difficult to exert a significant effect; if the Si content is more than 4 wt%, the brittleness of the coating is liable to be excessive. In a more preferred embodiment, the Si content may be in the range of 2 wt% to 4 wt%, within which a coating having a better overall performance may be obtained.
The alloy coating contains Mo, the Mo can reduce diffusion in the alloy by improving diffusion activation energy, so that the interatomic bonding force is enhanced, the hardness and the high-temperature strength of the alloy are improved, and the Mo can also promote the formation of a Laves phase in the coating, so that the high-temperature oxidation resistance and the corrosion resistance of the alloy coating are further improved. In addition, Mo can cover the catalytic active centers on the surface of the metal tube so as to reduce the adhesion of a surface carbon layer during operation, thereby being also beneficial to improving the anti-coking performance of the coating. In some embodiments, the content of Mo in the alloy coating may be 10 wt% to 30 wt%. If the content of Mo is less than 10 wt%, the formation of Laves phase is affected, and the catalytic active center on the surface of the metal pipe is difficult to cover, resulting in the reduction of the high-temperature oxidation resistance, corrosion resistance and coking resistance of the coating; if the content of Mo is more than 30wt%, the mechanical properties of the coating are affected, resulting in a decrease in the creep properties of the coating. In a more preferred embodiment, the Mo content may be in the range of 10 wt% to 25 wt%, within which range good compatibility of high temperature corrosion resistance, long lasting high temperature strength and plasticity of the alloy is achieved.
In some embodiments, the Ni content in the alloy coating is 25 wt% to 35 wt%. Within the content range, the alloy coating with better structure stability and high-temperature performance can be obtained. In a more preferred embodiment, the Ni content is 25 wt% to 30 wt%.
In some embodiments, the Cr content of the alloy coating is between 15 wt% and 25 wt%. Within the content range, the alloy coating with excellent comprehensive mechanical and corrosion resistance can be obtained. Too low Cr results in greatly reduced oxidation and corrosion resistance of the alloy coating, while too high Cr addition strongly promotes the precipitation of TCP (TCP) phase, thereby impairing the mechanical properties of the alloy. In a more preferred embodiment, the Cr content of the alloy coating is between 15 wt% and 20 wt%.
In some embodiments, the Al content in the alloy coating is 3wt% to 9 wt%. Within the content range, alloy coatings with excellent comprehensive properties can be obtained. Al is Al which forms a strengthening phase and is dense2O3Essential elements of the protective film. Higher Al content can reduce the depletion rate of the Al-rich phase, which is beneficial for improving the long-term oxidation resistance of the coating, but too high Al content can result in too high brittleness of the coating. In a more preferred embodiment, the Al content in the alloy coating is 5 wt% to 8 wt%.
In some embodiments, the Y content in the alloy coating is 0.1 wt% to 0.5 wt%. Within the content range, the adhesiveness of the oxide film can be effectively improved, and the high-temperature oxidation resistance and the hot corrosion resistance of the coating are improved. However, the solubility of Y in the alloy is low, segregation can be formed at the grain boundary and the like when the addition amount is too large, and during the oxidation process, the segregation position is easy to be preferentially oxidized to form a local internal oxidation area, so that the high-temperature oxidation resistance and the hot corrosion resistance of the coating are reduced. In a more preferred embodiment, the Y content in the alloy coating is 0.3wt% to 0.5 wt%.
In one embodiment, the alloy coating has the following chemical composition:
Ni:25wt％～35wt％，
Mo:10wt％～30wt％，
Cr:15wt％～25wt％，
Al:3wt％～9wt％，
Si:1wt％～4wt％，
Y:0.1wt％～0.5wt％，
and Co: Bal. (balance).
In the present disclosure, the thickness of the alloy coating layer may be 50 to 350 μm, and the metal substrate can be effectively protected and the better bonding strength can be obtained within the thickness range. More preferably, the thickness of the alloy coating layer may be 100 to 300 μm.
The alloy coating has higher bonding strength (for example, more than 40 MPa) with a base material, has unique capabilities of high-temperature oxidation resistance, sulfur resistance, chlorine corrosion resistance, high heat conductivity and thermal shock resistance, and is suitable for being sprayed on a material containing H2S、SO2And the service life of the pipe fitting mechanism in the fields of energy conservation, emission reduction, environmental protection and the like can be effectively prolonged on the surface of metal parts (such as the inner wall of a riser of a coke oven) made of corrosive high-temperature gas such as HCl and the like.
The alloy coatings of the present disclosure may be made using thermal spray techniques.
In a preferred embodiment, an atmospheric plasma spraying technology is adopted to deposit CoNiMoCrAlSiY powder on the surface of a base material to obtain a CoNiMoCrAlSiY alloy coating.
The substrate is not particularly limited, and may be, for example, a metal substrate. The alloy coatings of the present disclosure are particularly suitable for spraying on H-containing materials2S、SO2And the surface of a metal piece in a corrosive high-temperature gas environment such as HCl.
Prior to spraying, the substrate is preferably subjected to a surface pretreatment such as grit blasting, cleaning, compressed air blow drying.
The CoNiMoCrAlSiY powder can have the same composition as the CoNiMoCrAlSiY alloy coating. The CoNiMoCrAlSiY powder is prepared by the following method: an atomization powder preparation method.
The particle size of the CoNiMoCrAlSiY powder can be 25-60 mu m.
The process parameters of the atmospheric plasma spraying technology can comprise: the plasma gas argon flow is 30-60 slpm, the plasma gas hydrogen flow is 4-10 slpm, the spraying current is 300-600A, the voltage is 30-75V, the powder feeding carrier gas argon flow is 3-4 slpm, the powder feeding speed is 30-60 g/min, and the spraying distance is 80-130 mm, preferably 120 mm. By adopting the process parameters, the powder can be fully melted, and the liquid drops can be fully spread, so that the coating with a compact structure can be obtained.
The present invention will be described in detail by way of examples. It is also to be understood that the following examples are illustrative of the present invention and are not to be construed as limiting the scope of the invention, and that certain insubstantial modifications and adaptations of the invention by those skilled in the art may be made in light of the above teachings. The specific process parameters and the like of the following examples are also only one example of suitable ranges, i.e., those skilled in the art can select the appropriate ranges through the description herein, and are not limited to the specific values exemplified below.
In the following examples, the preparation method of the CoNiMoCrAlSiY alloy powder comprises the following steps: the atomization powder preparation method is characterized in that metal raw materials are firstly smelted into alloy melt, and then the alloy melt is injected into a tundish positioned above an atomization nozzle. When passing through the nozzle, the alloy melt meets the high-speed airflow and is atomized into fine molten drops, and the atomized molten drops are rapidly solidified into alloy powder in the closed atomizing barrel.
The bonding strength test method comprises the following steps: the test was carried out in HB 5476 using a universal material tester.
The method for testing the thermal conductivity of the coating comprises the following steps: and testing the thermal diffusion coefficient of the coating by using a laser thermal conductivity instrument, and obtaining the thermal conductivity of the coating by a formula thermal conductivity which is a thermal diffusion system multiplied by specific heat multiplied by density.
Example 1
(1) The substrate is a superalloy. Pretreating the surface of the metal base material to be sprayed: sand blasting, ultrasonic cleaning and compressed air blow drying.
(2) And depositing CoNiMoCrAlSiY alloy powder on the surface of the metal base material by adopting an atmospheric plasma process. The alloy powder comprises the following components: 25 wt%, Mo: 10 wt%, Cr: 15 wt%, Al: 6 wt%, Si: 2 wt%, Y: 0.5 wt%, Co: and (4) the balance. The spraying parameters are as follows: the flow of argon is 40slpm, the flow of hydrogen is 9slpm, the current is 600A, the power is 45kW, the flow of powder feeding carrier gas is 3.0slpm, the powder feeding speed is 35g/min, and the spraying distance is 120 mm.
FIG. 1 is a digital photograph and a cross-sectional SEM image of the resulting sample, with a coating thickness of about 110 μm, which was tightly bonded to the substrate. The bonding strength of the sample is tested, and the test value is 61.2 +/-1.5 MPa. The thermal conductivity of the coating is 19.4W/(m.K) (600 ℃), which shows that the coating has better heat-conducting property, and the oxidation weight gain of the coating in an air medium is 0.34g/cm after being tested for 100h at 900 DEG C2The coating has good high-temperature oxidation resistance.
Example 2
The preparation method is the same as that of example 1, the obtained sample is subjected to thermal shock for 50 times (900 ℃ -room temperature), and fig. 2 is a digital photo and a cross-section SEM image of the coating sample after thermal shock. After thermal shock, the coating is complete and has no phenomena of cracks, stripping and the like. And (5) testing the bonding strength of the sample subjected to thermal shock, wherein the testing value is 52.9 +/-4.2 MPa.
Example 3
(1) The base material is a solid ascending pipe part for raw gas sensible heat recovery engineering.
(2) And depositing CoNiMoCrAlSiY alloy powder on the inner wall of the treated riser for the raw coke oven gas sensible heat recovery project by adopting an atmospheric plasma process. The alloy powder comprises the following components: 25 wt%, Mo: 10 wt%, Cr: 15 wt%, Al: 6 wt%, Si: 2 wt%, Y: 0.5 wt%, Co: and (4) the balance. The spraying parameters are as follows: the flow rate of argon is 35slpm, the flow rate of hydrogen is 5slpm, the current is 400A, the power is 32kW, the flow rate of powder feeding carrier gas is 3.0slpm, and the powder feeding speed is 35 g/min.
(3) The obtained riser with the inner wall coated with the coating is in service for 1 year under the actual working condition. After service, the riser is subjected to anatomical analysis, and the cross-section SEM image of the intercepted coating sample is shown in figure 3. The coating is intact after service and is still tightly combined with the base material.
Example 4
The difference from example 1 is that the alloy powder components are Ni: 25 wt%, Mo: 10 wt%, Cr: 15 wt%, Al: 3wt%, Si: 1 wt%, Y: 0.1 wt%, Co: and (4) the balance. Coating structureCompact and tightly combined with the base material. The oxidation weight gain of the coating in an air medium is 0.36g/cm after being tested for 100h at 900 DEG C2。
Example 5
The difference from example 1 is that Ni: 35 wt%, Mo: 30wt%, Cr: 20 wt%, Al: 9 wt%, Si: 4 wt%, Y: 0.5 wt%, Co: and (4) the balance. The coating has compact structure and is tightly combined with the base material. The oxidation weight gain of the coating in an air medium is 0.42g/cm when the coating is tested at 900 ℃ for 100h2。
Example 6
The difference from example 1 is that the alloy powder components are Ni: 30wt%, Mo: 20 wt%, Cr: 20 wt%, Al: 6 wt%, Si: 3wt%, Y: 0.3wt%, Co: and (4) the balance. The coating has compact structure and is tightly combined with the base material. The oxidation weight gain of the coating in an air medium is 0.37g/cm after being tested for 100h at 900 DEG C2。
Example 7
The difference from the example 1 is that the spraying parameters are as follows: the flow rate of argon gas is 57slpm, the flow rate of hydrogen is 7slpm, the current is 580A, the voltage is 74V, the flow rate of powder feeding carrier gas is 3.0slpm, the powder feeding speed is 40g/min, and the spraying distance is 120 mm. The coating has compact structure, is tightly combined with the base material, and has the bonding strength of 62.3 +/-2.0 MPa.
Comparative example 1
For comparison, the NiAl alloy coating was prepared using atmospheric plasma spray technology. The shape and size of the sample, the preparation of the coating and the test method were the same as in example 1. Fig. 4 is a digital photograph thereof. The bonding strength of the sample is tested, and the test value is 35.9 +/-3.5 MPa. The thermal conductivity of the coating is 64.2W/(m.K) (600 ℃), and the oxidation weight gain of the coating in an air medium is 0.63g/cm after the coating is tested for 100h at 900 DEG C2。
Comparative example 2
For comparison, a CoNiCrAlY alloy coating was prepared using an atmospheric plasma spray technique. The alloy powder comprises the following components: 32 wt%, Cr: 21 wt%, Al: 8 wt%, Y: 0.5 wt%, Co: and (4) the balance. The shape and size of the sample, the preparation of the coating and the test method were the same as in example 1. Fig. 5 is a digital photograph thereof. The bonding strength of the sample is tested, and the test value is 51.0 +/-3.2 MPa. Is coated onThe oxidation weight gain of the alloy is 0.43g/cm in an air medium at 900 ℃ for 100h2。
Comparative example 3
The difference from example 1 is that the alloy powder components are Ni: 25 wt%, Mo: 3wt%, Cr: 15 wt%, Al: 6 wt%, Si: 2 wt%, Y: 0.5 wt%, Co: and (4) the balance. The bonding strength of the sample is tested, and the test value is 51.8 +/-4.0 MPa. The oxidation weight gain of the coating in an air medium is 0.41g/cm after being tested for 100h at 900 DEG C2。
Comparative example 4
The difference from example 1 is that the alloy powder components are Ni: 25 wt%, Mo: 35 wt%, Cr: 15 wt%, Al: 6 wt%, Si: 2 wt%, Y: 0.5 wt%, Co: and (4) the balance. The coating is in an air medium, and the coating is seriously peeled after being tested for 100 hours at 900 ℃.
Comparative example 5
The difference from example 1 is that the alloy powder components are Ni: 25 wt%, Mo: 10 wt%, Cr: 15 wt%, Al: 6 wt%, Y: 0.5 wt%, Co: and (4) the balance. The bonding strength of the coating is 54.0 +/-2.5 MPa.
Comparative example 6
The difference from example 1 is that the alloy powder components are Ni: 25 wt%, Mo: 10 wt%, Cr: 15 wt%, Al: 6 wt%, Si: 8 wt%, Y: 0.5 wt%, Co: and (4) the balance. Fig. 6 is a cross-sectional SEM image of the coated sample. The surface layer of the coating has partial structure stripping phenomenon, which indicates that the coating is too brittle.
Claims (8)
1. A hot-sprayed alloy coating with high-temperature oxidation resistance, sulfur resistance, chlorine corrosion resistance, coking resistance and high bonding strength is characterized in that the component of the alloy coating is CoNiMoCrAlSiY, wherein the ratio of Ni: 25 wt% -35 wt%, Mo: 10 wt% -30 wt%, Cr: 15 wt% -25 wt%, Al: 3wt% -9 wt%, Si: 1 wt% -4 wt%, Y: 0.1 wt% -0.5 wt%, Co: and (4) the balance.
2. The alloy coating of claim 1, wherein the alloy coating comprises: ni: 25 wt% -30 wt%, Mo: 10 wt% -25 wt%, Cr: 15 wt% -20 wt%, Al: 5 wt% -8 wt%, Si: 2-4 wt%, Y: 0.3wt% -0.5 wt%, Co: and (4) the balance.
3. The alloy coating according to claim 1, wherein the alloy coating thickness is 50 to 350 μm.
4. A method for producing an alloy coating according to any one of claims 1 to 3, characterized in that a conimocrally alloy coating is sprayed onto the surface of the substrate by means of a thermal spraying technique.
5. The production method according to claim 4, wherein the thermal spraying technique is an atmospheric plasma spraying technique.
6. The method of claim 5, wherein the process parameters of the atmospheric plasma spray technique include: the plasma gas argon flow is 30-60 slpm, the plasma gas hydrogen flow is 4-10 slpm, the spraying current is 300-600A, the voltage is 30-75V, the powder feeding carrier gas argon flow is 3-4 slpm, and the powder feeding speed is 30-60 g/min.
7. The production method according to any one of claims 4 to 6, wherein the substrate is a metal substrate.
8. The method of claim 7, wherein the substrate is an inner wall of a riser of a coke oven.
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| High Temperature Corrosion of CoNiCrAlY-Si Alloys in an Air-Na2SO4-NaCl Gas Atmosphere;Toto Sudiro;《Materials Transactions》;20110126;第52卷(第3期);第433页"2. Experimental Procedures"、第434页"3. Results and Discussion" * |
| 等离子体喷涂CoNiCrAlY涂层的抗氧化性能;姜杰;《第十二届国际热喷涂研讨会论文暨第十三届全国热喷涂年会论文》;20091117;第5-6页"2、实验方法" * |
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